EP1580287B1 - Stahl mit hervorragender zerspanbarkeit undherstellungsverfahren dafür - Google Patents

Stahl mit hervorragender zerspanbarkeit undherstellungsverfahren dafür Download PDF

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EP1580287B1
EP1580287B1 EP03772791A EP03772791A EP1580287B1 EP 1580287 B1 EP1580287 B1 EP 1580287B1 EP 03772791 A EP03772791 A EP 03772791A EP 03772791 A EP03772791 A EP 03772791A EP 1580287 B1 EP1580287 B1 EP 1580287B1
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Prior art keywords
steel
inv
machinability
mns
production
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French (fr)
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EP1580287A1 (de
EP1580287A4 (de
Inventor
Masayuki C/O NIPPON STEEL CORPORATION HASHIMURA
Atsushi C/O NIPPON STEEL CORPORATION MIZUNO
Kenichiro C/O NIPPON STEEL CORPORATION NAITO
Hiroshi C/O NIPPON STEEL CORPORATION HAGIWARA
Kohichi C/O NIPPON STEEL CORPORATION ISOBE
Hiroshi C/O NIPPON STEEL CORPORATION HIRATA
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Nippon Steel Corp
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Nippon Steel Corp
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Priority claimed from JP2002332668A external-priority patent/JP4264247B2/ja
Priority claimed from JP2002332707A external-priority patent/JP4213948B2/ja
Priority claimed from JP2002332658A external-priority patent/JP4323778B2/ja
Priority claimed from JP2003374511A external-priority patent/JP4264329B2/ja
Priority claimed from JP2003374489A external-priority patent/JP4348163B2/ja
Priority claimed from JP2003374517A external-priority patent/JP4348164B2/ja
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • JP 2000 160 284 discloses a free cutting steel with good machinability in which the Mn/S ratio is regulated to ⁇ 1.70.
  • Japanese Unexamined Patent Publication (Kokai) No. 11-222646 proposes a method of improving chip disposal by establishing the presence of at least 30 sulfides of 20 ⁇ m or more alone or groups of sulfides comprised of pluralities of sulfides connected substantially linearly in lengths of 20 ⁇ m or more in an observation field of a cross-section of 1 mm 2 in the rolling direction.
  • the dispersion of sulfides of the submicron level most effective for machinability in practice, including the method of production is not alluded to. Further, not much can be expected in view of the ingredients as well.
  • the present invention provides steel having a good surface roughness and a method of production of the same which avoid problems in hot rolling and hot forging while improving both the tool life and surface roughness and giving a machinability at least equivalent to that of conventional low carbon and lead free-machining steel.
  • Cutting is a fracture phenomenon of breaking off chips. Promotion of this is one point.
  • the inventors caused embrittlement of the matrix so as to facilitate fracture and thereby extend tool life and also suppressed nonuniformity in the steel to a minimum so as to cause a fracture phenomenon stable even on the micro level and thereby suppress roughness of the cut surface.
  • the inventors took note of the distribution of pearlite in steel and caused C to uniformly disperse as fine pearlite (strictly speaking cementite) in steel so as to cause stable fracture and thereby create a cut surface with no roughness and provided a method of production enabling this.
  • the gist of the present invention is as follows:
  • the present invention is characterized by causing embrittlement of the matrix so as to obtain a sufficient machinability, in particular a good surface roughness, without adding lead and by adding a large amount of B to obtain good lubrication of the contact surfaces of the tool/cut material. Further, a relatively large amount of S is also added and the ratio of amounts of addition of Mn and S is precisely controlled to cause them to fine disperse. Further, for the microstructure of the steel, the pearlite seen in conventional carbon steel is controlled.
  • this is steel superior in machinability comprised of chemical ingredients, suppressed in the amount of addition of C, suppressed in the precipitation of coarse pearlite, or, in the case of including too much C, suppressed in coarse pearlite grains by heat treatment, that is, suppressed in pearlite bands often seen in natural cooling.
  • C is related to the basic strength of the steel and the amount of oxygen in the steel, so has a great effect on the machinability. If a large amount of C is added to raise the strength, the machinability declines, so the upper limit was made 0.2%. On the other hand, to prevent the generation of hard oxides lowering the machinability and suppress the pinholes in the solidification process or other damage by dissolved oxygen at a high temperature, it is necessary to control the amount of oxygen to a suitable amount. If just reducing the amount of C by blow refining, not only does the cost mount, but also a large amount of oxygen remains in the steel and becomes a cause of pinholes and other problems. Therefore, the lower limit was made a 0.005% amount of C able to easily prevent pinholes and other problems. The preferable lower limit of the amount of C is 0.05%.
  • MnS improves the machinability, but stretched MnS is one cause of anisotropy at casting. Large MnS should be avoided, but addition of a large amount is preferable from the viewpoint of improvement of the machinability. Therefore, it is preferable to cause the MnS to finely disperse. For improvement of the machinability to at least that of the conventional sulfur free-machining steel in the case of no addition of Pb, addition of at least 0.03% is necessary. On the other hand, if over 1%, not only cannot production of coarse MnS be avoided, but also cracks occur during production due to deterioration of the casting properties and hot deformation properties due to the FeS etc., so this was made the upper limit.
  • B has the effect of improving the machinability when precipitated as BN. This effect is not remarkable at 0.0005% or less, while the effect is saturated even if B is added in an amount of over 0.05%. If too much BN is precipitated, conversely cracks occur during production due to deterioration of the casting properties and hot deformation properties. Therefore, the range was made over 0.0005 to 0.05%.
  • O total 0
  • total 0 forms bubbles during cooling in the case of presence in the free state and becomes causes of pinholes. Further, control is necessary for softening the oxides and suppressing hard oxides harmful to machinability. Further, oxides are utilized as nuclei for precipitation at the time of fine dispersion of MnS. If under 0.0005%, sufficient fine dispersion of MnS is not possible, crude MnS is generated, and there is a detrimental effect on the mechanical properties as well, so the lower limit was made 0.0005%. Further, if the amount of oxygen exceeds 0.035%, bubbles form during casting to cause pinholes, so the upper limit was made 0.035%.
  • Mn/S it is already known that this has a large effect on the hot ductility and that normally if Mn/S>3, the production efficiency is greatly reduced. The reason is the production of FeS.
  • this ratio can be reduced to Mn/S: 1.2 to 2.8. With an Mn/S of less than 1.2, a large amount of FeS is produced, the hot ductility is sharply reduced, and the production efficiency is greatly reduced.
  • FIG. 2 shows examples of observation of fine MnS in the cases where Mn/S ⁇ 2.8 and Mn/S>2.8 under a transmission type electron microscope using the replica method.
  • Mn/S>2.8 the result becomes only coarse MnS such as shown in FIG. 2(b) and the surface roughness cannot be reduced.
  • Mn/S:1.2 to 2.8 production of fine MnS such as shown in FIG. 2(a) is obtained.
  • MnS is an inclusion improving the machinability. By causing fine dispersion at a high density, the machinability is remarkably improved. To obtain this effect, it is necessary that the density of MnS of a circle equivalent diameter of 0.1 to 0.5 ⁇ m be at least 10,000/mm 2 .
  • the MnS sulfides are usually observed in distribution by an optical microscope and measured for dimensions and density. MnS sulfides of these dimensions cannot be confirmed by observation under an optical microscope. They can only be observed first by a transmission type electron microscope (TEM). They are sulfides mainly comprised of MnS of dimensions where a clear difference can be recognized under TEM observation even if there is no difference in dimensions and density under observation by an opticalmicroscope. In the present invention, this is controlled and the form of presence is converted to numerical values to differentiate it from the prior art.
  • TEM transmission type electron microscope
  • the density of MnS of a circle equivalent diameter of 0.1 to 0.5 ⁇ m be at least 10,000/mm 2 .
  • BN normally easily precipitates at the crystal boundaries and has difficulty uniformly dispersing in the matrix. Therefore, it is not possible to cause uniform embrittlement of the matrix required for improving the machinability and not possible to sufficiently obtain the effect of BN.
  • MnS which forms sites for precipitation of BN and is also effective for improving machinability, to uniformly disperse in the matrix.
  • MnS includes not only pure MnS, but also inclusions including mainly MnS and having sulfides of Fe, Ca, Ti, Zr, Mg, REM, etc. dissolved in or bonded with the MnS for copresence, inclusions like MnTe where elements other than S form compounds with Mn and dissolve in or bond with MnS for copresence, and the above inclusions precipitated using oxides as nuclei.
  • Mn sulfide-type inclusions able to be expressed by the chemical formula (Mn, X) (S,Y) (where X: sulfide forming elements other than Mn and Y: element binding with Mn other than S).
  • Nb also forms a carbonitride and can strengthen the steel by secondary precipitation hardening. At 0.005% or less, there is no effect on raising the strength, while if added in an amount over 0.2%, a large amount of carbonitrides is precipitated and conversely the mechanical properties are prevented, so this was made the upper limit.
  • Mo is an element imparting temper softening resistance and improving the quenchability. At under 0.05%, that effect cannot be detected, while even if added at over 1.0%, the effect is saturated, so the range of addition was made 0.05% to 1.0%.
  • W forms carbides and can strengthen the steel by secondary precipitation hardening. If 0.05% or less, there is no effect on raising the strength, while if added over 1.0%, a large amount of carbides precipitate and conversely the mechanical properties are prevented, so this was made the upper limit.
  • Cu strengthens the ferrite and is effective for improving the quenchability and improves the corrosion resistance. If under 0.01%, this effect cannot be observed, while even if added over 2.0%, the effect is saturated in the point of the mechanical properties, so this was made the upper limit. In particular, the hot ductility is reduced and defects are easily caused at the time of rolling, so it is preferable to simultaneously add Ni.
  • Sn has the effect of causing embrittlement of ferrite, extending the tool life, and improving the surface roughness. If less than 0.005%, this effect cannot be observed, while even if added over 2.0%, the effect is saturated in the point of the mechanical properties, so this was made the upper limit.
  • Ca is a deoxygenizing element. It not only produces soft oxides and improves the machinability, but also dissolves in the MnS and reduces the transformation ability and acts to suppress elongation of the MnS shape even with rolling and hot forging. Therefore, it is an element effective for reducing anisotropy. If less than 0.0002%, the effect is not remarkable, while even if adding 0.005% or more, not only does the yield become extremely poor, but also a large amount of hard CaO is produced and conversely the machinability is reduced. Therefore, the range is defined as 0.0002 to 0.005%.
  • Zr is a deoxygenizing element and produces oxides.
  • the oxides form nuclei for precipitation of MnS and are effective for the fine, uniform diffusion of MnS. Further, it dissolves in MnS to reduce the deformation ability and acts to suppress elongation of the MnS shape even with hot rolling or hot forging. Therefore, it is an element effective for reduction of anisotropy. If less than 0.0005%, the effect is not remarkable, while even if added in 0.1% or more, not only does the yield become extremely poor, but also large amounts of ZrO 2 , ZrS, etc. are produced and conversely the machinability is reduced. Therefore, the range of addition was defined as 0.0005 to 0.1%. Note that when trying to finely disperse MnS, compound addition of Zr and Ca is preferable.
  • Mg is a deoxygenizing element and produces oxides.
  • the oxides form nuclei for precipitation of MnS and are effective for the fine, uniform dispersion of MnS. It is an element effective for reduction of anisotropy. If less than 0.0003%, the effect is not remarkable, while even if added in 0.005% or more, not only does the yield become extremely poor, but also the effect is saturated. Therefore, the range of addition was defined as 0.0003 to 0.005%.
  • Bi and Pb are elements effective for improving machinability. Their effects are not observed at 0.005% or less, while even if added in amounts over 0.5%, not only do the effects of improvement of machinability become saturated, but also the hot forgeability drops and easily becomes a cause of defects.
  • the fine dispersion of sulfides having MnS as a main ingredient and having BN compound precipitated is effective for improvement of the machinability.
  • the cooling rate can be easily obtained by controlling the size of the cross-section of the casting mold, the casting speed, etc. to suitable values. This may be applied to the continuous casting method and the pouring method.
  • the "cooling rate” referred to here means the speed at the time of cooling from the liquid phase line temperature to the solid phase line temperature in the billet thickness of Q part (greater part: half depth to the core from the surface).
  • BN dissolves in austenite at 1000°C or more.
  • the BN precipitated in the process from the casting to the rough rolling remains at the grain boundaries and compound precipitation as sulfides having MnS as a main ingredient and having BN compound precipitated is not possible.
  • the once dissolved BN easily compound precipitates as nuclei for precipitation of MnS sulfides. If finally rolling at 1000°C or less, compound precipitation of sulfides mainly comprised of BN and MnS no longer easily occurs.
  • the inventors adjusted the steel ingredients or thermal history to suppress the area ratio of pearlite grains of a grain size of 1 ⁇ m or more in an observation field of a measurement field of 4 mm 2 and investigate the critical region where a good surface roughness is obtained, whereupon they learned that deterioration of the surface roughness is suppressed by making the area ratio of pearlite grains of 1 ⁇ m or more a ratio of not more than 5%.
  • FIG. 2 shows the relationship between the area ratio of pearlite and the surface roughness.
  • the free-machining steel according to the present invention has extremely little of such a structure appearing black.
  • the result is strictly speaking tempered martensite or tempered bainite.
  • the carbides are not pearlite (in other words, a striped structure of plate-shaped cementite and ferrite), but cementite grains.
  • ferrous carbides will be referred to all together as "pearlite”.
  • the thermal history after hot rolling it is important to cool from a temperature of above the A 3 point after hot rolling to 550°C or less by a cooling rate of at least 0.5°C/sec.
  • the alloy elements are added in large amounts as with stainless steel, even if the cooling rate is slower than 0.5°C/sec, pearlite bands are not formed.
  • the cooling rate is defined as 0.5°C/sec.
  • heat treatment for holding at a temperature of 750°C or less may be performed to make the structure of the free-machining steel more homogeneous.
  • the holding temperature and the holding time should be determined so as to give a hardness satisfying the demands of the users.
  • the holding temperature T 2 °C exceeds 750°C, transformation to austenite starts, so if the cooling rate at cooling again is slow, pearlite bands end up being produced. Therefore, the holding temperature T 2 °C was made 750°C or less. Further, wire drawing or other secondary working is often applied at a later step, so it is preferable to adjust the temperature T 2 °C so as to give a hardness suitable for handling in the later step.
  • the holding time industrially speaking, at 3 minutes or less, there is almost no change in hardness etc. compared with almost no holding, so the time is preferably made at least this.
  • the holding time at the temperature T1°C of up to 550°C after rapid cooling for preventing coarse pearlite should also be considered.
  • a temperature T1°C of 550°C or less after rapid cooling for preferably at least 5 minutes uniform ferrite transformation can be promoted without relation to the dimensions of the material or segregation bands. By doing this, after this, even if raising the temperature to the holding temperature T 2 °C ( ⁇ 750°C), coarse pearlite or pearlite bands will not be generated.
  • the examples marked as "Normal.” are held at 920°C for at least 10 min and then air-cooled.
  • the examples of the invention marked as "QT" are inserted into a water tank at the rear end of the rolling line and rapidly cooled from 920°C, then held by annealing at 700°C for at least 1 hour.
  • the pearlite area ratio was adjusted by this.
  • steels with a low amount of C can be reduced in area ratio of pearlite even with normalization.
  • the machinability of the material shown in Examples 1 to 81 of Table 1 to Table 6 was evaluated by a drilling test of the conditions shown in Table 7.
  • the machinability was evaluated at the maximum cutting speed (so-called VL1000, unit m/min) enabling cutting up to a cumulative hole depth of 1000 mm.
  • the chips be small in curvature at the time of curling or that they be broken. Therefore, chips extending long curled 3 or more turns by a radius of curvature over 20 mm are deemed defective. Chips with a large number of turns and small radius of curvature or chips with a large radius of curvature and length not reaching 100 mm are deemed good.
  • Table 1 Chemical ingredients wt% Ex. Class C Si Mn P S B total-N total-O V Nb Cr Mo W Ni Cu Sn Zn 1 Inv. ex. 0.023 0.004 1.69 0.072 0.52 0.0080 0.0079 0.0167 2 Inv. ex.
  • Table 10 (continuation 1 of Table 9), Table 11 (continuation 2 of Table 9), Table 12 (continuation 3 of Table 9), Table 13 (continuation 4 of Table 9), and Table 14 (continuation 5 of Table 9) were produced by a 270 t converter, then casted at a cooling rate of 10 to 100°c/min.
  • the billet was bloomed, then further rolled to ⁇ 50 mm. Further, the rest was melted in a 2 t vacuum melting furnace and rolled to ⁇ 50 mm. At this time, the cooling rate of the billet was adjusted by changing the cross-sectional dimensions of the casting mold.
  • the machinability of the material was evaluated by a drilling test of the conditions shown in Table 7 and plunge cutting of the conditions shown in Table 8.
  • MnS of a size which cannot be confirmed at the optical microscope level is clearly different in dimensions and density in the inventions of the examples and comparative examples by observation of TEM replicas.
  • Table 10 Table 12, and Table 14 are as follows.
  • the cutting resistance was measured by attaching a piezoelectric dynamometer (made by Kistler) to the turret of a lathe, setting the tool on it to give the same position as normal cutting, and performing plunge cutting Due to this, measurement is possible using the principal force component and thrust force component applied to the tool as voltage signals.
  • the cutting speed, feed speed, and other cutting conditions are similar to those for evaluation of the cut surface roughness.
  • the chips be small in curvature at the time of curling or that they be broken. Therefore, chips extending long curled 3 or more turns by a radius of curvature over 20 mm are deemed defective. Chips with a large number of turns and small radius of curvature or chips with a large radius of curvature and length not reaching 100 mm are deemed good.
  • the present invention enables use for automobile parts and general machinery parts have superior properties of tool life and cut surface roughness at the time of cutting and disposal of chips.

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Claims (6)

  1. Stahl mit ausgezeichneter Zerspanbarkeit, der in Gew.-% aufweist:
    C: 0,005 bis 0,2 %,
    Si: 0,001 bis 0,5 %,
    Mn: 0,2 bis 3,0 %,
    P: 0,001 bis 0,2 %,
    S: 0,03 bis 1,0 %,
    B: 0,0005 bis 0,05 %,
    Ges.-N: 0,002 bis 0,02 %,
    Ges.-O: 0,0005 bis 0,035 %,
    optional ein oder mehrere Elemente, die ausgewählt sind aus:
    V: 0,05 bis 1,0 %,
    Nb: 0,005 bis 0,2 %,
    Cr: 0,01 bis 2,0 %,
    Mo: 0,05 bis 1,0 %,
    W: 0,5 bis 1,0 %,
    Ni: 0,05 bis 2,0 %,
    Cu: 0,01 bis 2,0 %,
    Sn: 0,005 bis 2,0 %,
    Zn: 0,0005 bis 0,5 %,
    Ti: 0,0005 bis 0,1 %,
    Ca: 0,0002 bis 0,005 %,
    Zr: 0,0005 bis 0,1 %,
    Mg : 0,0003 bis 0,005 %,
    Te: 0,0003 bis 0,05 %,
    Bi : 0,005 bis 0,5 %,
    Pb: 0,01 bis 0,5 % und
    Al: ≤ 0,015 %
    sowie als Rest Eisen und unvermeidliche Verunreinigungen, wobei der Stahl folgendes erfüllt: Mn/S im Stahl beträgt 1,2 bis 2,8, ein Flächenverhältnis von Perlit mit einer Korngröße über 1 µm in einer Mikrostruktur des Stahls beträgt höchstens 5 % und eine Dichte von MnS mit 0,1 bis 0,5 µm Äquivalenzdurchmesser an einem Querschnitt parallel zu einer Walzrichtung des Stahlmaterials, die anhand einer Extraktionsreplik ermittelt und mit einem Transmissionselektronenmikroskop beobachtet wird, beträgt mindestens 10.000/mm2.
  2. Stahl mit ausgezeichneter Zerspanbarkeit nach Anspruch 1, wobei der Stahl in Gew.-% Mn: 0,3 bis 3,0 % und S: 0,1 bis 1,0 % enthält.
  3. Stahl mit ausgezeichneter Zerspanbarkeit nach Anspruch 1, wobei der Stahl dadurch gekennzeichnet ist, daß ferner die Menge von S auf 0,25 bis 0,75 Gew.-% und die Menge von B auf 0,002 bis 0,014 Gew.-% beschränkt ist, daß er Mengen von S und B in einem von A, B, C und D gemäß Fig. 4 umgebenen Bereich enthält, in dem die Gehalte von S und B die nachfolgende Gleichung (1) erfüllen, und daß er Sulfide mit in MnS ausgeschiedenem BN enthält: ( B - 0 , 008 ⁢ ) 2 / 0 , 006 2 + ( S - 0 , 5 ⁢ ) 2 / 0 , 25 2 ≤ 1
    Figure imgb0004
  4. Verfahren zur Herstellung von Stahl mit ausgezeichneter Zerspanbarkeit nach einem der Ansprüche 1 bis 3, wobei das Verfahren zur Stahlherstellung gekennzeichnet ist durch Gießen einer Stahlschmelze mit den Stahlbestandteilen nach Anspruch 1, anschließendes Abkühlen mit einer Abkühlungsgeschwindigkeit von 10 bis 100 °C/min, und nach Warmwalzen des Gußstahls erfolgendes Abkühlen mit einer Abkühlungsgeschwindigkeit von mindestens 0,5 °C/s in einem Bereich von einem A3-Punkt auf 550 °C.
  5. Verfahren zur Herstellung von Stahl mit ausgezeichneter Zerspanbarkeit nach einem der Ansprüche 1 bis 3, wobei das Verfahren zur Stahlherstellung gekennzeichnet ist durch Gießen einer Stahlschmelze mit den Stahlbestandteilen nach Anspruch 1, anschließendes Abkühlen mit einer Abkühlungsgeschwindigkeit von 10 bis 100 °C/min, Warmwalzen des Gußstahls durch Einschränken einer Fertigwarmwalztemperatur auf mindestens 1000 °C und anschließendes Abkühlen mit einer Abkühlungsgeschwindigkeit von mindestens 0,5 °C/s in einem Bereich von einem A3-Punkt auf 550 °C.
  6. Verfahren zur Herstellung von Stahl mit ausgezeichneter Zerspanbarkeit nach Anspruch 4 oder 5, wobei das Verfahren zur Stahlherstellung gekennzeichnet ist durch Einschränken einer Erwärmungstemperatur zur Härteeinstellung auf höchstens 750 °C nach der Abkühlung nach dem Warmwalzen.
EP03772791A 2002-11-15 2003-11-14 Stahl mit hervorragender zerspanbarkeit undherstellungsverfahren dafür Expired - Fee Related EP1580287B1 (de)

Applications Claiming Priority (19)

Application Number Priority Date Filing Date Title
JP2002332668A JP4264247B2 (ja) 2002-11-15 2002-11-15 被削性に優れる鋼およびその製造方法
JP2002332658A JP4323778B2 (ja) 2002-11-15 2002-11-15 被削性に優れる鋼の製造方法
JP2002332668 2002-11-15
JP2002332665 2002-11-15
JP2002332665 2002-11-15
JP2002332695 2002-11-15
JP2002332707 2002-11-15
JP2002332669 2002-11-15
JP2002332707A JP4213948B2 (ja) 2002-11-15 2002-11-15 被削性に優れる鋼
JP2002332669 2002-11-15
JP2002332695 2002-11-15
JP2002332658 2002-11-15
JP2003374489A JP4348163B2 (ja) 2002-11-15 2003-11-04 被削性に優れる鋼及びその製造方法
JP2003374511A JP4264329B2 (ja) 2002-11-15 2003-11-04 被削性に優れる鋼
JP2003374489 2003-11-04
JP2003374517A JP4348164B2 (ja) 2002-11-15 2003-11-04 被削性に優れる鋼
JP2003374511 2003-11-04
JP2003374517 2003-11-04
PCT/JP2003/014547 WO2004050932A1 (ja) 2002-11-15 2003-11-14 被削性に優れる鋼とその製造方法

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EP1580287A1 EP1580287A1 (de) 2005-09-28
EP1580287A4 EP1580287A4 (de) 2006-07-05
EP1580287B1 true EP1580287B1 (de) 2008-01-16

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EP1580287A1 (de) 2005-09-28
DE60318745T2 (de) 2009-01-15
WO2004050932A1 (ja) 2004-06-17
KR100708430B1 (ko) 2007-04-18
DE60318745D1 (de) 2008-03-06
EP1580287A4 (de) 2006-07-05
US20060013720A1 (en) 2006-01-19
US20090050241A1 (en) 2009-02-26
TWI249579B (en) 2006-02-21
US8137484B2 (en) 2012-03-20

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